High-strength steel having superior brittle crack arrestability, and production method therefor

ABSTRACT

Provided are high-strength steel having superior brittle crack arrestability and a production method therefor. The high-strength steel comprises 0.05-0.1 wt % of C, 0.9-1.5 wt % of Mn, 0.8-1.5 wt % of Ni, 0.005-0.1 wt % of Nb, 0.005-0.1 wt % of Ti, 0.1-0.6 wt % of Cu, 0.1-0.4 wt % of Si, at most 100 ppm of P, and at most 40 ppm of S with the remainder being Fe and other inevitable impurities, and has microstructures including one structure selected from the group consisting of a single-phase structure of ferrite, a single-phase structure of bainite, a complex-phase structure of ferrite and bainite, a complex-phase structure of ferrite and pearlite, and a complex-phase structure of ferrite, bainite, and pearlite. The high-strength steel has high yield strength and superior brittle crack arrestability.

TECHNICAL FIELD

The present disclosure relates to a high-strength steel having excellent brittle crack arrestability and a method of manufacturing the same.

BACKGROUND ART

Recently, in designing structures used in domestic and international shipbuilding, marine engineering, architecture and civil engineering fields, the development of an extremely thick steel having high strength properties is required.

When high-strength steel is used in designing structures, since such structures may be lightened, an economical benefit may be obtained; and since a thickness of a steel sheet may be reduced, ease of machining and welding operations may be secured simultaneously.

In general, for a high-strength steel, when an extremely thick steel sheet is manufactured, due to a reduction in a total reduction ratio, sufficient deformation does not occur in a central portion, so a structure of a central portion may become coarse. Therefore, as hardenability is increased, a low temperature transformation phase such as bainite, or the like, is generated.

In addition, due to the structure having been coarsened, it may be difficult to secure impact toughness in a central portion.

In detail, in the case of brittle crack arrestability referring to stability of a structure, when a high-strength steel is applied to a major structure such as a ship, or the like, cases in which guaranteed levels of brittle crack arrestability are required have increased. However, when a low temperature transformation phase is generated in a central portion, a phenomenon in which brittle crack arrestability is significantly reduced occurs. Therefore, it may be difficult to improve brittle crack arrestability of an extremely thick high-strength steel.

Meanwhile, in the case of a high-strength steel having yield strength of 390 MPa or more, in order to improve brittle crack arrestability, various techniques have been introduced, such as the application of surface cooling during finish rolling for refinement of a grain size in a surface layer, grain size adjusting by applying bending stress during rolling, refinement of a surface layer by two phase region rolling, and the like.

However, various techniques are helpful in refining a structure in a surface layer, but do not solve the problem of impact toughness degradation due to coarsening of a structure in a central portion. Therefore, the various techniques are not fundamental measures for brittle crack arrestability.

In addition, because the techniques themselves are expected to significantly reduce productivity when applied to a general production system, such techniques are problematic in terms of commercial applications.

DISCLOSURE Technical Problem

An aspect of the present disclosure is to provide a high-strength steel having excellent brittle crack arrestability.

Another aspect of the present disclosure is to provide a method of manufacturing a high-strength steel having excellent brittle crack arrestability.

Technical Solution

According to an aspect of the present disclosure, a high-strength steel having excellent brittle crack arrestability includes 0.05 wt % to 0.1 wt % of carbon (C), 0.9 wt % to 1.5 wt % of manganese (Mn), 0.8 wt % to 1.5 wt % of nickel (Ni), 0.005 wt % to 0.1 wt % of niobium (Nb), 0.005 wt % to 0.1 wt % of titanium (Ti), 0.1 wt % to 0.6 wt % of copper (Cu), 0.1 wt % to 0.4 wt % of silicon (Si), 100 ppm or less of phosphorous (P), 40 ppm or less of sulfur (S), and the remainder being iron (Fe) and other inevitably contained impurities, the high-strength steel having a microstructure including one structure selected from the group consisting of a single-phase structure of ferrite, a single-phase structure of bainite, a complex-phase structure of ferrite and bainite, a complex-phase structure of ferrite and pearlite, and a complex-phase structure of ferrite, bainite, and pearlite, and having a thickness of 50 mm or more.

The contents of Cu and Ni may be set such that a Cu/Ni weight ratio may be 0.6 or less, in detail, 0.5 or less.

In the high-strength steel, a grain size having a high-angle boundary of 15 degrees or more, measured in an EBSD method, in a central portion of the steel may be 30 μm (micrometers) or less.

In the high-strength steel, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction in a region of the high-strength steel in a range of 20% of an overall steel thickness based on a position equal to ½ of the steel thickness may be 40% or less.

In the high-strength steel, yield strength may be 390 MPa or more.

According to another aspect of the present disclosure, a method of manufacturing a high-strength steel having excellent brittle crack arrestability includes: reheating a slab at 950° C. to 1100° C., the slab including 0.05 wt % to 0.1 wt % of carbon (C), 0.9 wt % to 1.5 wt % of manganese (Mn), 0.8 wt % to 1.5 wt % of nickel (Ni), 0.005 wt % to 0.1 wt % of niobium (Nb), 0.005 wt % to 0.1 wt % of titanium (Ti), 0.1 wt % to 0.6 wt % of copper (Cu), 0.1 wt % to 0.4 wt % of silicon (Si), 100 ppm or less of phosphorous (P), 40 ppm or less of sulfur (S), and the remainder being iron (Fe) and other inevitably contained impurities, and then rough rolling the slab at a temperature of 1100° C. to 900° C.; obtaining a steel sheet having a thickness of 50 mm or more by finish rolling a rough-rolled bar at a temperature of 850° C. to Ar₃; and cooling the steel sheet to a temperature of 700° C. or less, wherein a temperature difference between a central portion and a surface of the slab or bar before the rough rolling is 70° C. or more during the rough rolling.

During the rough rolling, a reduction ratio per pass with respect to three final passes may be 5% or more, and a total cumulative reduction ratio may be 40% or more, preferably.

A crystal grain size of a central portion of the bar in a thickness direction before the finish rolling after the rough rolling may be 200 μm or less, preferably 150 μm or less, and more preferably 100 μm or less.

A reduction ratio during the finish rolling may be set such that a ratio of a slab thickness (mm)/a steel sheet thickness (mm) after finish rolling may be 3.5 or above, preferably 3.8 or above.

The cooling of the steel sheet may be performed at a cooling rate of a central portion of the steel sheet in a thickness direction of 2° C./s or more.

The cooling of the steel sheet may be performed at an average cooling rate from 3° C./s to 300° C./s.

In addition, the solution of the problems described above does not list all the features of the present disclosure.

Various features, advantages, and effects of the present disclosure will be more fully understood by reference to the following specific embodiments

Advantageous Effects

According to an exemplary embodiment in the present disclosure, a high-strength steel having high yield strength and excellent brittle crack arrestability may be obtained.

DESCRIPTION OF DRAWINGS

FIG. 1 is an image of a central portion of Inventive steel 1 in a thickness direction, captured with an optical microscope.

BEST MODE FOR INVENTION

The inventors conducted research and experiments into improving yield strength and brittle crack arrestability of a thick steel having a thickness of 50 mm or more, and the present disclosure has been proposed based on the results thereof.

According to the present disclosure, a steel composition, a structure, a texture, and manufacturing conditions of a steel are controlled, so yield strength and brittle crack arrestability of a steel having a thick thickness are further improved.

A main concept in the present disclosure is as follows.

1) To improve strength through solid solution strengthening, a steel composition is appropriately controlled. In detail, for solid solution strengthening, the content of each of Mn, Ni, Cu, and Si is optimized.

2) To improve strength through hardenability improvement, a steel composition is appropriately controlled. In detail, to improve hardenability, in addition to the content of carbon, the content of each of Mn, Ni, and Cu is optimized.

As described above, by improving hardenability, a fine structure to a central portion of a thick steel having a thickness of 50 mm or more even at a cooling rate, which is slow, is secured.

3) Preferably, to improve strength and brittle crack arrestability, a structure of a steel is refined. In detail, a structure of a central portion of a steel is refined.

As described above, the structure of a central portion of a steel is refined, so strength is improved due to strengthening by grain refinement, while brittle crack arrestability is improved by significantly reducing the generation and propagation of cracks.

4) Preferably, to improve brittle crack arrestability, a texture of a steel is controlled.

Taking into consideration that a crack is propagated in a width direction of a steel, that is, in a direction perpendicular to a rolling direction, and a brittle fracture surface of a body-centered cubic (BCC) structure is a (100) plane, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction is significantly reduced.

In detail, a texture of an area of a central portion in which a microstructure is relatively coarse in comparison with a surface is controlled.

As described above, the texture of a steel, in detail, the texture of an area of a central portion of a steel, is controlled. Even when a crack is generated, propagation of the crack is significantly reduced, so brittle crack arrestability is improved.

5) Preferably, to allow a structure of a steel to be further refined, rough rolling conditions are controlled.

In detail, during rough rolling, a pressing condition is controlled, and a sufficient temperature difference between a central portion and a surface is secured, so a fine structure is secured to a central portion of a steel.

Hereinafter, a high-strength steel having excellent brittle crack arrestability, one aspect of the present disclosure, will be described in detail.

According to an aspect of the present disclosure, a high-strength steel having excellent brittle crack arrestability includes 0.05 wt % to 0.1 wt % of C, 0.9 wt % to 1.5 wt % of Mn, 0.8 wt % to 1.5 wt % of Ni, 0.005 wt % to 0.1 wt % of Nb, 0.005 wt % to 0.1 wt % of Ti, 0.1 wt % to 0.6 wt % of Cu, 0.1 wt % to 0.4 wt % of Si, 100 ppm or less of P, 40 ppm or less of S, and the remainder being iron (Fe) and other inevitably contained impurities, and has a microstructure including one structure selected from the group consisting of a single-phase structure of ferrite, a single-phase structure of bainite, a complex-phase structure of ferrite and bainite, a complex-phase structure of ferrite and pearlite, and a complex-phase structure of ferrite, bainite, and pearlite.

Hereinafter, a steel component and a component range of the present disclosure will be described.

C (Carbon): 0.05% to 0.10% (Hereinafter, the Contents of Respective Components Refer to Weight %)

C is the most important element in securing basic strength, so C needs to be contained in a steel in an appropriate range. In order to obtain such an additive effect, C is preferably added in an amount of 0.05% or more.

However, when the content of C exceeds 0.10%, due to the generation of a large amount of martensite-austenite constituent (MA), high strength of ferrite itself, and generation of a large amount of a low temperature transformation phase, or the like, low temperature toughness may be reduced. Thus, the content of C is preferably limited to 0.05% to 0.10%, more preferably limited to 0.061% to 0.091%, and most preferably limited to 0.065% to 0.085%.

Mn (Manganese): 0.9% to 1.5%

Mn is a useful element for improving strength due to solid solution strengthening and for improving hardenability to allow a low temperature transformation phase to be generated. In order to obtain an effect described above, Mn is preferably added in an amount of 0.9% or more.

However, when the content of Mn exceeds 1.5%, due to an excessive increase in hardenability, the generation of upper bainite and martensite is promoted. In addition, segregation in a central portion is caused, so a coarse low temperature transformation phase is generated. Thus, impact toughness and brittle crack arrestability are reduced.

Thus, the content of Mn is preferably limited to 0.9% to 1.5%, more preferably limited to 0.97% to 1.39%, and most preferably limited to 1.15% to 1.30%.

Ni (Nickel): 0.8% to 1.5%

Ni is an important element, allowing dislocation cross-slip to be easily performed at a low temperature to improve impact toughness, and improving hardenability to improve strength. In order to obtain an effect described above, Ni is preferably added in an amount of 0.8% or more. However, when Ni is added in an amount of 1.5% or more, hardenability is excessively increased, so a low temperature transformation phase is generated. Thus, toughness may be reduced and manufacturing costs may be increased. In this case, an upper limit of the content of Ni is preferably limited to 1.5%.

The content of Ni is more preferably limited to 0.89% to 1.42% and most preferably limited to 1.01% to 1.35%.

Nb (Niobium): 0.005% to 0.1%

Nb is precipitated in the form of NbC or NbCN, thereby improving strength of a base material.

In addition, Nb, dissolved during reheating at a high temperature, is significantly finely precipitated in the form of NbC during rolling, so recrystallization of austenite is suppressed. Thus, a structure may be refined.

Thus, Nb is preferably added in an amount of 0.005% or more. However, when Nb is added excessively, a brittle crack may be caused in an edge of a steel. In this case, an upper limit of the content of Nb is preferably limited to 0.1%.

The content of Nb is more preferably limited to 0.012% to 0.028% and most preferably limited to 0.018% to 0.024%.

Ti (Titanium): 0.005% to 0.1%

Ti is precipitated as TiN during reheating, and thus inhibits growth of a crystal grain in a base material and in a weld heat affected zone, thereby significantly improving low temperature toughness. In order to obtain an additive effect described above, Ti is preferably added in an amount of 0.005% or more.

However, when Ti is added in an amount exceeding 0.1%, a continuous casting nozzle may be clogged, or low temperature toughness may be reduced by crystallization of a central portion. In this case, the content of Ti is preferably limited to 0.005% to 0.1%.

The content of Ti is more preferably limited to 0.009% to 0.024% and most preferably limited to 0.011% to 0.018%.

P (Phosphorous): 100 Ppm or Less, Sulfur (S): 40 Ppm or Less

P and S are elements causing brittleness in a grain boundary or causing brittleness by forming a coarse inclusion. In order to improve brittle crack arrestability, P is preferably limited to 100 ppm or less and S is preferably limited to 40 ppm or less.

Si (Silicon): 0.1% to 0.4%

Si improves strength of a steel and has a strong deoxidizing effect, and thus is an essential element in producing clean steel. In order to obtain an effect described above, Si is preferably added in an amount of 0.1% or more. However, when a large amount of Si is added, a coarse MA phase is generated, so brittle crack arrestability may be reduced. In this case, an upper limit of the content of Si is preferably limited to 0.4%.

The content of Si is more preferably limited to 0.22% to 0.32% and most preferably limited to 0.25% to 0.3%.

Cu (Copper): 0.1% to 0.6%

Cu is a main element in improving strength of a steel by improving hardenability and causing solid solution strengthening, and is a main element in increasing a yield strength due to generation of ε (epsilon) Cu precipitate when tempering is applied. Thus, Cu is preferably added in an amount of 0.1% or more. However, when a large amount of Cu is added, in a steelmaking process, due to hot shortness, a crack in a slab may be generated. In this case, an upper limit of the content of Cu is preferably limited to 0.6%.

The content of Cu is more preferably limited to 0.21% to 0.51% and most preferably is limited to 0.18% to 0.3%.

The contents of Cu and Ni are set such that a Cu/Ni weight ratio is 0.6 or less and preferably 0.5 or less.

When the Cu/Ni weight ratio is set as described above, a surface quality may be further improved.

According to an exemplary embodiment, iron (Fe) may be provided as a remainder thereof.

On the other hand, in an ordinary manufacturing process, non-intended impurities may be inevitably present, from a raw material or a surrounding environment, which may not be excluded.

The impurities may be known to those skilled in the art, and thus, may not be particularly described in this specification.

The steel according to an exemplary embodiment may have a microstructure including a single structure selected from the group consisting of a single-phase structure of ferrite, a single-phase structure of bainite, a complex-phase structure of ferrite and bainite, a complex-phase structure of ferrite and pearlite, and a complex-phase structure of ferrite, bainite, and pearlite.

The ferrite is preferably polygonal ferrite or acicular ferrite, and the bainite is preferably granular bainite.

For example, as the contents of Mn and Ni increase, fraction of acicular ferrite and granular bainite increases, so strength also increases.

When a microstructure of the steel is a complex-phase structure containing pearlite, fraction of pearlite is preferably limited to 20% or less.

In the steel, a grain size having a high-angle boundary of 15 degrees or more, measured in an EBSD method, in a central portion may be preferably 30 μm or less.

As described above, the grain size of a structure of a central portion of the steel is refined to be 30 μm or less, so strength is improved due to strengthening by grain refinement, while brittle crack arrestability is improved by significantly reducing the generation and propagation of cracks.

Preferably, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction in a region of the high-strength steel in a range of 20% of an overall steel thickness based on a position equal to ½ of the steel thickness may be 40% or less.

Main reasons for controlling a texture as described above are as follows.

A crack is propagated in a width direction of a steel, that is, in a direction perpendicular to a rolling direction, and a brittle fracture surface of a body-centered cubic structure (BCC) is a (100) plane.

In this case, in an exemplary embodiment, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction is significantly reduced.

In detail, a texture of an area of a central portion in which a microstructure is relatively coarse in comparison with a surface is controlled.

As described above, a texture of a steel and, particularly, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction in a region of the high-strength steel in a range of 20% of an overall steel thickness based on a position equal to ½ of the steel thickness is controlled to be 40% or less. Even when a crack is generated, propagation of the crack is significantly reduced, so brittle crack arrestability is improved.

The steel preferably has a yield strength of 390 MPa or more.

The steel has a thickness of 50 mm or more, preferably has a thickness of 50 mm to 100 mm, and more preferably has a thickness of 80 mm to 100 mm.

Hereinafter, a method of manufacturing a high-strength steel having excellent brittle crack arrestability, another aspect of the present disclosure, will be described in detail.

According to another aspect of the present disclosure, a method of manufacturing a high-strength steel having excellent brittle crack arrestability includes: reheating a slab including 0.05 wt % to 0.1 wt % of C, 0.9 wt % to 1.5 wt % of Mn, 0.8 wt % to 1.5 wt % of Ni, 0.005 wt % to 0.1 wt % of Nb, 0.005 wt % to 0.1 wt % of Ti, 0.1 wt % to 0.6 wt % of Cu, 0.1 wt % to 0.4 wt % of Si, 100 ppm or less of P, 40 ppm or less of S, and the remainder being iron (Fe) and other inevitably contained impurities at 950° C. to 1100° C. and then rough rolling the slab at a temperature of 1100° C. to 900° C.; obtaining a steel sheet by finish rolling a rough-rolled bar at a temperature of 850° C. to Ar₃; and cooling the steel sheet to a temperature of 700° C. or less. When the rough rolling is performed, a temperature difference between a central portion and a surface of the slab or bar before the rough rolling is 70° C. or more.

Reheating of Slab

A slab is reheated before rough rolling.

A reheating temperature of a slab is preferably set to be 950° C. or more, to dissolve carbonitride of Ti and/or Nb formed during casting. In addition, in order to sufficiently dissolve carbonitride of Ti and/or Nb, it is more preferably to heat at 1000° C. or more. However, when the slab is reheated to an excessively high temperature, austenite may be coarsened. Thus, an upper limit of the reheating temperature is preferably limited to 1100° C.

Rough Rolling

The slab, having been reheated, is rough rolled.

A rough rolling temperature is preferably a temperature (Tnr) at which recrystallization of austenite is stopped or more. Due to rolling, effects in which a casting structure such as a dendrite formed during casting or the like is destroyed and a size of austenite is reduced may be obtained. To obtain the effects described above, the rough rolling temperature is preferably limited to 1100° C. to 900° C.

In an exemplary embodiment, during rough rolling, a temperature difference between a central portion and a surface of the slab or bar immediately before the rough rolling should be 70° C. or more.

As described above, as the temperature difference between a central portion and a surface is given during rough rolling, a surface of the slab or bar maintains a temperature lower than that of a central portion. While the temperature difference exists, when rough rolling is performed, more deformation occurs in a central portion in which a temperature is relatively high than in the surface in which a temperature is relatively low. Thus, a crystal grain size of a central portion is more refined. In this case, preferably, an average grain size of a central portion may be maintained to be 30 μm or less.

In this technique, a phenomenon, in which the surface in which a temperature is relatively low has strength higher than that of a central portion in which a temperature is relatively high, so more deformation occurs in a central portion having relatively low strength, is used. To effectively give more deformation in a central portion, a temperature difference between a central portion and a surface is preferably 100° C. or more and more preferably 100° C. to 300° C.

Here, the temperature difference between a central portion and a surface of the slab or bar indicates a difference between a temperature of a surface of the slab or bar measured immediately before rough rolling, and a temperature of a central portion, calculated in consideration of a cooling condition and a thickness of the slab or bar immediately before rough rolling.

Measuring of a temperature of a surface and a thickness of the slab is performed before first rough rolling, and measuring of a temperature of a surface and a thickness of the bar is performed before rough rolling, starting from a second process of rough rolling.

In addition, when rough rolling is performed in two or more passes, a temperature difference between a central portion and a surface of the slab or bar indicates that a temperature difference, in which a temperature difference for each pass of rough rolling is measured and a total average value is calculated, is 70° C. or more.

In an exemplary embodiment, in order to refine a structure of a central portion during rough rolling, with respect to three final passes during rough rolling, a reduction ratio per pass is 5% or more, and a total cumulative reduction ratio is preferably 40% or more.

In an exemplary embodiment, in order to refine a structure of a central portion during rough rolling, with respect to three final passes during rough rolling, a reduction ratio per pass is 5% or more, and a total cumulative reduction ratio is preferably 40% or more.

When rough rolling is performed, in a structure re-crystallized due to initial rolling, growth of a crystal grain occurs due to a high temperature. However, when three final passes are performed, while waiting for rolling, a bar is air-cooled, so a growth rate of the crystal grain slows down. Thus, during rough rolling, reduction ratios of three final passes are significant for a grain size of a final microstructure.

In addition, when a reduction ratio per a pass of rough rolling is lowered, sufficient deformation is not transferred to a central portion, so toughness degradation caused by coarsening of a central portion may occur. Thus, a reduction ratio per pass of three final passes is preferably limited to 5% or more.

On the other hand, for refinement of a structure of a central portion, a total cumulative reduction ratio during rough rolling is preferably set to be 40% or more.

Finish Rolling

The bar having been rough rolled is finish rolled at 850° C. to Ar₃ (a ferrite transformation start temperature), so a steel sheet is obtained.

In order to obtain a further refined microstructure, a finish rolling temperature of finish rolling is preferably 850° C. or less.

When finish rolling is performed, an austenite structure becomes a deformed austenite structure.

A crystal grain size of a central portion of a bar before finish rolling after the rough rolling is 200 μm or less, preferably 150 μm or less, and more preferably 100 μm or less.

The crystal grain size of a central portion of a bar before finish rolling after the rough rolling may be controlled according to a rough rolling condition, or the like.

As described above, when a crystal grain size of a central portion of a bar before finish rolling after the rough rolling is controlled, due to refinement of an austenite crystal grain, a final microstructure is refined, so yield/tensile strength may be increased and low temperature toughness may be improved.

A reduction ratio during the finish rolling may be set such that a ratio of a slab thickness (mm)/a steel sheet thickness (mm) after finish rolling is 3.5 or above, preferably 3.8 or more.

As described above, when a reduction ratio during finish rolling is controlled, as a reduction amount increases during rough rolling and finish rolling, due to refinement of a final microstructure, yield/tensile strength may be increased and low temperature toughness may be improved. Moreover, due to a reduction in a grain size of a central portion in a thickness direction, toughness of a central portion may be improved.

After finish rolling, a steel sheet has a thickness of 50 mm or more, preferably has a thickness of 50 mm to 100 mm, and more preferably has a thickness 80 mm to 100 mm.

Cooling

After finish rolling, a steel sheet is cooled to 700° C. or less

When a cooling end temperature exceeds 700° C., a microstructure is not properly formed, so yield strength may be 390 Mpa or less.

Cooling of the steel sheet may be performed at a cooling rate of a central portion of the steel sheet in a thickness direction of 2° C./s or more. When a cooling rate of a central portion of the steel sheet in a thickness direction is less than 2° C./s, a microstructure is not properly formed, so yield strength may be 390 Mpa or less.

In addition, cooling of the steel sheet may be performed at an average cooling rate from 3° C./s to 300° C./s.

MODE FOR INVENTION

Hereinafter, an exemplary embodiment in the present disclosure will be described in further detail with reference to Embodiments.

It should be noted, however, that the following embodiments are intended to illustrate the present disclosure in more detail and not to limit the scope of the invention.

In other words, the scope of the invention is determined by the matters described in the claims and matters able to be reasonably deduced therefrom.

Embodiment 1

After a steel slab with a thickness of 400 mm having a composition of Table 1 was reheated at a temperature of 1050° C., rough rolling was performed at a temperature of 1020° C., so a bar was manufactured. When a slab was rough rolled, an average temperature difference between a central portion and a surface is illustrated in Table 2, a cumulative reduction ratio of 50% is equally applied.

The average temperature difference between a central portion and a surface during rough rolling of Table 2 refers to a difference between a temperature of a surface of a slab or bar measured immediately before rough rolling, and a temperature of a central portion calculated in consideration of an amount of water sprayed to a bar and a slab thickness immediately before rough rolling, and is a result in which a temperature difference for each pass of rough rolling is measured and a total average value is calculated.

A thickness of the bar having been rough rolled was 180 mm, and a crystal grain size before finish rolling after rough rolling was 80 μm.

After the rough rolling, finish rolling was performed at a finish rolling temperature of 770° C., so a steel sheet having a thickness of Table 2 was obtained, and cooling was performed to a temperature of 700° C. or less at a cooling rate of 5° C./sec thereafter.

With respect to the steel sheet manufactured as described above, a microstructure, yield strength, an average grain size of a central portion measured in EBSD, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction in a region of the high-strength steel in a range of 20% of an overall steel thickness based on a position equal to ½ of the steel thickness, a Kca value (a brittle crack arrestability coefficient) were investigated, and a result thereof is illustrated in Table 2.

A Kca value of Table 2 is a value evaluated by performing an ESSO test with respect to a steel sheet.

TABLE 1 Steel Composition (Weight %) Cu/Ni Steel weight Grade C Si Mn Ni Cu Ti Nb P (ppm) S (ppm) ratio Inventive 0.061 0.23 1.25 0.89 0.35 0.015 0.019 75 16 0.39 steel 1 Inventive 0.082 0.31 1.36 0.95 0.44 0.016 0.017 77 25 0.46 steel 2 Inventive 0.054 0.32 1.09 1.26 0.36 0.009 0.023 82 34 0.29 steel 3 Inventive 0.072 0.22 1.39 1.13 0.21 0.024 0.012 65 19 0.19 steel 4 Inventive 0.069 0.29 1.17 1.21 0.45 0.02 0.019 68 22 0.36 steel 5 Inventive 0.091 0.31 0.97 1.42 0.51 0.019 0.028 71 31 0.36 steel 6 Comparative 0.072 0.25 1.21 0.97 0.36 0.017 0.026 69 16 0.37 steel 1 Comparative 0.12 0.29 1.32 1.12 0.39 0.017 0.023 59 13 0.35 steel 2 Comparative 0.068 0.61 1.39 1.08 0.45 0.019 0.027 55 25 0.42 steel 3 Comparative 0.077 0.32 1.95 1.32 0.21 0.026 0.019 67 26 0.16 steel 4 Comparative 0.062 0.19 1.21 2.2 0.35 0.021 0.031 49 30 0.16 steel 5 Comparative 0.072 0.22 1.06 1.11 0.48 0.016 0.022 130 65 0.43 steel 6

TABLE 2 Temperature difference between Average central grain portion and *Microstructure, size (μm) surface Product phase Yield of Steel during rough thickness fraction (001) strength central Kca(N/mm^(1.5), Grade rolling (° C.) (mm) (%) texture (Mpa) portion @−10° C.) Inventive 165 85 PF + P(16%) 23 396 21.2 9012 steel 1 Inventive 203 90 AF 18 442 12.7 8554 steel 2 Inventive 112 85 AF + GB(24%) 26 509 15.6 7356 steel 3 Inventive 215 85 AF + GB(20%) 19 492 13.9 7855 steel 4 Inventive 188 90 AF + GB(38%) 21 521 17.7 6918 steel 5 Inventive 196 100 PF + P(17%) 16 401 20.9 6522 steel 6 Comparative 21 85 PF + P(18%) 43 398 35.4 4564 steel 1 Comparative 116 90 UB 42 579 38.3 3866 steel 2 Comparative 154 85 AF + UB(21%) 32 534 25.6 4211 steel 3 Comparative 201 90 UB 42 607 34.2 3901 steel 4 Comparative 165 90 GB, UB(22%) 31 551 31.2 3244 steel 5 Comparative 123 95 AF + GB(17%) 29 498 23.1 4855 steel 6 *PF: Polygonal Ferrite, P: Pearlite, AF: Acicular Ferrite, GB: Granular Bainite, UB: Upper Bainite, Phase fraction (%): Volume %

As illustrated in Table 2, in the case of Comparative steel 1, an average temperature difference between a central portion and a surface during rough rolling presented in the present disclosure is controlled to be less than 70° C. When rough rolling is performed, as sufficient deformation is not given to a central portion, a grain size of a central portion is 35.4 μm, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction in a region of the high-strength steel in a range of 20% of an overall steel thickness based on a position equal to ½ of the steel thickness is 40% or more, and a Kca value measured at −10° C. does not exceed 6000, required for steel for shipbuilding according to the related art.

In the case of Comparative steel 2, the content of C has a value higher than an upper limit of the content of C according to the present disclosure. When rough rolling is performed, through cooling, a grain size of austenite of a central portion is refined, but upper bainite is generated. Thus, a grain size of a final microstructure is 38.3 μm, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction in a region of the high-strength steel in a range of 20% of an overall steel thickness based on a position equal to ½ of the steel thickness is 40% or more. Moreover, upper bainite in which brittleness may easily occur is included as a base structure, so a Kca value is a value of 6000 or less at −10° C.

In the case of Comparative steel 3, the content of Si has a value higher than an upper limit of the content of Si according to the present disclosure. When rough rolling is performed, through cooling, a grain size of austenite of a central portion is refined, but upper bainite is partially generated in a central portion. Moreover, as a large amount of Si is added, a large amount of a MA structure is coarsely generated, so a Kca value is a value of 6000 or less at −10° C.

In the case of Comparative steel 4, the content of Mn has a value higher than an upper limit of the content of Mn according to the present disclosure. Due to high hardenability, a microstructure of a base material is upper bainite. When rough rolling is performed, through cooling, a grain size of austenite of a central portion is refined, but a grain size of a final microstructure is 34.2 μm, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction in a region of the high-strength steel in a range of 20% of an overall steel thickness based on a position equal to ½ of the steel thickness is 40% or more, and a Kca value is a value of 6000 or less at −10° C.

In the case of Comparative steel 5, the content of Ni has a value higher than an upper limit of the content of Ni according to the present disclosure. Due to high hardenability, a microstructure of a base material is granular bainite and upper bainite. When rough rolling is performed, through cooling, a grain size of austenite of a central portion is refined, but a grain size of a final microstructure is 31.2 μm, and a Kca value is a value of 6000 or less at −10° C.

In the case of Comparative steel 6, the content of each of P and S has a value higher than an upper limit of the content of each of P and S according to the present disclosure. Even when other conditions are satisfied with conditions presented in the present disclosure, due to high P and S, brittleness may occur. Thus, a Kca value is a value of 6000 or less at −10° C.

On the contrary, in the cases of Inventive steel 1 through 6, satisfying a composition range according to the present disclosure and in which a grain size of austenite of a central portion is refined through cooling during rough rolling, yield strength satisfies 390 MPa or more, and a grain size of a central portion satisfies 30 μm or less. Moreover, a complex-phase structure of ferrite and pearlite, a single-phase structure of acicular ferrite, or a complex-phase structure of acicular ferrite and granular bainite is included as a microstructure.

Moreover, an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction in a region of the high-strength steel in a range of 20% of an overall steel thickness based on a position equal to ½ of the steel thickness is 40% or less, and a Kca value satisfies a value of 6000 or more at −10° C.

FIG. 1 is an image of a central portion of Inventive steel 1 in a thickness direction captured with an optical microscope. As illustrated in FIG. 1, it is confirmed that a structure of a central portion in a thickness direction is refined.

Embodiment 2

Except for a change in a Cu/Ni weight ratio of a steel slab as illustrated in Table 3, a steel sheet was manufactured with the same composition and manufacturing conditions as Inventive steel 2 of Embodiment 1, surface properties of the steel sheet having been manufactured were investigated, and a result thereof is illustrated in Table 3.

In Table 3, surface properties of the steel sheet refer to a measure of whether a star crack in a surface occurred due to hot shortness.

TABLE 3 Steel Composition (wt %) Cu/Ni Steel P S weight Surface Grade C Si Mn Ni Cu Ti Nb (ppm) (ppm) ratio Properties Inventive 0.082 0.31 1.36 0.84 0.41 0.016 0.017 77 25 0.48 Non-occurrence steel 7 Inventive 0.95 0.44 0.46 Non-occurrence steel 2 Inventive 0.37 0.12 0.32 Non-occurrence steel 8 Inventive 0.28 0.10 0.35 Non-occurrence steel 9 Comparative 0.23 0.18 0.78 Occurrence steel 7 Comparative 0.48 0.33 0.71 Occurrence steel 8

As illustrated in Table 3, when a Cu/Ni weight ratio is properly controlled, it is confirmed that surface properties of a steel sheet are improved.

Embodiment 3

Except for a change in a crystal grain size (μm) before finish rolling after rough rolling as illustrated in Table 4, a steel sheet was manufactured in the same composition and manufacturing condition as Inventive steel 1 of Embodiment 1. Properties of an average grain size of a central portion of a steel sheet having been manufactured were investigated, and a result thereof is illustrated in Table 4.

TABLE 4 Crystal grain size (μm) before finish rolling after Average grain size (μm) of Steel Grade rough rolling central portion Inventive steel 1 80 21.2 Inventive steel 125 29.7 10 Inventive steel 107 25.6 11 Inventive steel 75 19.8 12 Inventive steel 155 21.5 13 Inventive steel 110 24.5 14

As illustrated in Table 4, as a crystal grain size of a central portion of a bar after rough rolling decreases, it is confirmed that an average grain size of a central portion is refined. Thus, it is expected that brittle crack propagation resistance is to be improved.

While exemplary embodiments with respect to a cutting device and a cutting method have been shown and described above, it will be apparent to those skilled in the art that modifications and variations could be made without departing from the scope of the present invention as defined by the appended claims. 

1. A high-strength steel having excellent brittle crack arrestability, comprising: 0.05 wt % to 0.1 wt % of carbon (C), 0.9 wt % to 1.5 wt % of manganese (Mn), 0.8 wt % to 1.5 wt % of nickel (Ni), 0.005 wt % to 0.1 wt % of niobium (Nb), 0.005 wt % to 0.1 wt % of titanium (Ti), 0.1 wt % to 0.6 wt % of copper (Cu), 0.1 wt % to 0.4 wt % of silicon (Si), 100 ppm or less of phosphorous (P), 40 ppm or less of sulfur (S), and the remainder being iron (Fe) and other inevitably contained impurities, the high-strength steel having a microstructure including one structure selected from the group consisting of a single-phase structure of ferrite, a single-phase structure of bainite, a complex-phase structure of ferrite and bainite, a complex-phase structure of ferrite and pearlite, and a complex-phase structure of ferrite, bainite, and pearlite, and having a thickness of 50 mm or more.
 2. The high-strength steel having excellent brittle crack arrestability of claim 1, wherein the contents of Cu and Ni are set such that a Cu/Ni weight ratio is 0.6 or less.
 3. The high-strength steel having excellent brittle crack arrestability of claim 1, wherein the ferrite is acicular ferrite or polygonal ferrite, and the bainite is granular bainite.
 4. The high-strength steel having excellent brittle crack arrestability of claim 1, wherein when the microstructure of the steel is a complex-phase structure including the pearlite, a fraction of pearlite is 20% or less.
 5. The high-strength steel having excellent brittle crack arrestability of claim 1, wherein in the high-strength steel, a grain size having a high-angle boundary of 15 degrees or more measured, in an electron backscattered diffraction (EBSD) method, in a central portion of a steel thickness, is 30 μm or less.
 6. The high-strength steel having excellent brittle crack arrestability of claim 1, wherein in the high-strength steel, yield strength is 390 MPa or more.
 7. The high-strength steel having excellent brittle crack arrestability of claim 1, wherein an area ratio of a (100) plane forming an angle within 15 degrees with respect to a plane perpendicular to a rolling direction in a region of the high-strength steel in a range of 20% of an overall steel thickness based on a position equal to ½ of the steel thickness is 40% or less.
 8. The high-strength steel having excellent brittle crack arrestability of claim 1, wherein a steel thickness is 80 mm to 100 mm.
 9. A method of manufacturing a high-strength steel having excellent brittle crack arrestability, the method comprising: reheating a slab to a temperature of 950° C. to 1100° C., the slab including 0.05 wt % to 0.1 wt % of carbon (C), 0.9 wt % to 1.5 wt % of manganese (Mn), 0.8 wt % to 1.5 wt % of nickel (Ni), 0.005 wt % to 0.1 wt % of niobium (Nb), 0.005 wt % to 0.1 wt % of titanium (Ti), 0.1 wt % to 0.6 wt % of copper (Cu), 0.1 wt % to 0.4 wt % of silicon (Si), 100 ppm or less of phosphorous (P), 40 ppm or less of sulfur (S), and the remainder being iron (Fe) and other inevitably contained impurities, and then rough rolling the slab at a temperature of 1100° C. to 900° C.; obtaining a steel sheet having a thickness of 50 mm or more by finish rolling a rough-rolled bar at a temperature of 850° C. to Ar₃; and cooling the steel sheet to a temperature of 700° C. or less, wherein a temperature difference between a central portion and a surface of the slab or bar before the rough rolling is 70° C. or more when the rough rolling is performed.
 10. The method of manufacturing a high-strength steel having excellent brittle crack arrestability of claim 9, wherein the contents of Cu and Ni are set such that a Cu/Ni weight ratio is 0.6 or less.
 11. The method of manufacturing a high-strength steel having excellent brittle crack arrestability of claim 9, wherein a temperature difference between a central portion in a thickness direction of the slab or bar and an outer surface of the slab or bar is 100° C. to 300° C.
 12. The method of manufacturing a high-strength steel having excellent brittle crack arrestability of claim 9, wherein a temperature difference between a central portion in a thickness direction and an outer surface of the slab or bar is a difference between a temperature of a surface of the slab or bar measured immediately before the rough rolling, and a temperature of a central portion calculated in consideration of a cooling condition and a thickness of the slab or bar immediately before the rough rolling.
 13. The method of manufacturing a high-strength steel having excellent brittle crack arrestability of claim 9, wherein the rough rolling is performed in two or more passes, and a temperature difference between a central portion in the thickness direction of the slab or bar and an outer surface of the slab or bar is a temperature difference in which a temperature difference therebetween for each pass of the rough rolling is measured and a total average value is calculated.
 14. The method of manufacturing a high-strength steel having excellent brittle crack arrestability of claim 9, wherein a reduction ratio per pass, with respect to three final passes when the rough rolling is performed, is 5% or more, and a total cumulative reduction ratio is 40% or more.
 15. The method of manufacturing a high-strength steel having excellent brittle crack arrestability of claim 9, wherein a crystal grain size of a central portion of the bar before the finish rolling after the rough rolling is 200 μm or less.
 16. The method of manufacturing a high-strength steel having excellent brittle crack arrestability of claim 9, wherein a reduction ratio during the finish rolling is set such that a ratio of a slab thickness (mm)/a steel sheet thickness (mm) after the finish rolling is 3.5 or above.
 17. The method of manufacturing a high-strength steel having excellent brittle crack arrestability of claim 9, wherein the cooling of the steel sheet is performed at a cooling rate of a central portion of the steel sheet of 2° C./s or more.
 18. The method of manufacturing a high-strength steel having excellent brittle crack arrestability of claim 9, wherein the cooling of the steel sheet is performed at an average cooling rate from 3° C./s to 300° C./s. 